US20190071748A1 - Method for temperature-treating a manganese steel intermediate product, and steel intermediate product which has been temperature-treated in a corresponding manner - Google Patents

Method for temperature-treating a manganese steel intermediate product, and steel intermediate product which has been temperature-treated in a corresponding manner Download PDF

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US20190071748A1
US20190071748A1 US16/085,361 US201716085361A US2019071748A1 US 20190071748 A1 US20190071748 A1 US 20190071748A1 US 201716085361 A US201716085361 A US 201716085361A US 2019071748 A1 US2019071748 A1 US 2019071748A1
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temperature
intermediate product
steel intermediate
manganese
annealing
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Friedrich Füreder-Kitzmüller
Reinhold Schneider
Daniel Krizan
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Voestalpine Stahl GmbH
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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium

Definitions

  • the present invention relates to a method of temperature treating a manganese steel intermediate product. It also relates to a specific alloy of a manganese steel intermediate product, which is temperature-treated by a special process to achieve a significantly reduced Lüders strain.
  • EP 16 162 073.7 filed on 23 Mar. 2016.
  • Mn manganese
  • Mn manganese
  • the manganese content in weight percent (wt. %) is often in the range between 3 and 12. Due to its microstructure, a medium-manganese steel has a high combination of tensile strength and elongation. Typical applications in the automotive industry are complex safety-relevant deep-drawn components.
  • FIG. 1 a classical, highly schematic diagram is shown, in which the elongation at break A 80 (also known as total elongation) is plotted in percent over the tensile strength in MPa.
  • the tensile strength is abbreviated here with R m .
  • the diagram of FIG. 1 gives an overview of the strength classes of currently used steel materials for the automotive industry. In general, the following statement applies: the higher the tensile strength R m of a steel alloy, the lower the total elongation A 80 of this alloy. In simple terms, it can be stated that the total elongation A 80 decreases with increasing tensile strength R m and vice versa. It is therefore necessary to find an optimal compromise between the total elongation A 80 and the tensile strength R m for each application.
  • steel alloys which have a high tensile strength R m of usually more than 1000 MPa.
  • R m tensile strength
  • This category includes the TBF (Trip Bainitic Ferrite) steels and the Q&P (Quenching & Partitioning) steels.
  • These high-strength AHSS steels have, for example, a manganese content in the range between 1.2 and 3 wt. % and a carbon content C which is between 0.05 and 0.25 wt. %.
  • the area designated by the reference numeral 3 in FIG. 1 the already mentioned medium-manganese steels are schematically summarized.
  • the area designated by the reference numeral 3 comprises medium-manganese steels having an Mn content of between 3 and 12 wt. % and a carbon content of ⁇ 1 wt. %.
  • FIG. 2 An exemplary tensile curve 4 (also called stress-strain curve) is shown in FIG. 2 .
  • the tension ⁇ in MPa
  • the tensile curve 4 shows an intermediate maximum 5, which is referred to as the upper yield strength (R eH ), followed by a plateau 6 .
  • the plateau 6 changes into a rising curve region.
  • the “length” of the plateau 6 is referred to as Lüders strain (A L ), as shown in FIG.
  • a steel product with such a pronounced yield strength can form undesirable Lüders bands (stretcher-strainer marks) on the surface of the components for the automobile industry. Therefore, the pronounced yield strength typically needs to be reduced by a re-rolling process.
  • the aftertreatment in a corresponding re-rolling plant (usually with a skin-pass mill) is also referred to as skin-pass rolling.
  • the object to develop a method for the production of manganese steel intermediate products in which the Lüders strain is less pronounced.
  • the manganese steel intermediate products should have no (measurable) Lüders strain.
  • the partial object of the invention is thus to find an alloy composition and a process for temperature treatment in order to increase the original austenite grain size and to manifest the increased austenite grains in the structure of the medium-manganese steels.
  • the invention aims in a different direction.
  • a double annealing process is used, which works with other temperatures and process procedures. Steel products made by the method of WO2014095082A1 have a pronounced yield strength.
  • the manganese steel alloy of the invention comprises:
  • the manganese steel intermediate products which have been produced from a melt of this manganese steel alloy are subjected within the scope of a temperature treatment according to the invention to a first temperature treatment process and a subsequent second temperature treatment process.
  • the first temperature treatment process is a high-temperature process in which the steel intermediate product is subjected during a first holding period to a first annealing temperature which is above a critical temperature limit (referred to as T KG ), wherein this critical temperature limit (T KG ) is defined as follows: T KG ⁇ (856 ⁇ S K *manganese content) degrees Celsius, and wherein S K is a slope value.
  • T KG critical temperature limit
  • the aforementioned formula which serves as a definition of the critical temperature limit (T KG ), states that the critical temperature limit (T KG ) decreases in the manganese range mentioned with increasing manganese content.
  • the second temperature treatment process is an annealing process in which the steel intermediate product is subjected to a second annealing temperature T 2 , which is in each case lower than the first annealing temperature T 1 .
  • the first annealing temperature T 1 shows in all embodiments a dependence on said manganese range of the alloy, which is defined as follows: T 1 ⁇ T KG .
  • Particularly preferred are embodiments of the invention at a critical temperature T K ⁇ (866 ⁇ S K *manganese content) degrees Celsius, where the following applies: S K 7.83 ⁇ 10%.
  • the first holding period is at least 10 seconds in all embodiments. Particularly preferably, the first holding period in all embodiments is between 10 seconds and 7000 minutes.
  • the second annealing temperature T 2 is in all embodiments in the range between the temperatures A 1 and A 3 .
  • the second temperature treatment process including the heating of the steel intermediate product, the holding the second annealing temperature and the cooling of the steel intermediate product, takes less than 6000 minutes. Preferably, this total time is even less than 5000 minutes.
  • the invention makes it possible to provide steel intermediate products having a Lüders strain A L which is less than 3% and preferably less than 1%.
  • the steel intermediate products of the invention preferably have an average primary austenite grain size greater than 3 ⁇ m in all embodiments.
  • the alloy of the steel intermediate products of the invention preferably has an average manganese content according to the invention, which means that the manganese content is in the range of 3 wt. % ⁇ Mn ⁇ 12 wt. %.
  • the manganese content in all embodiments is in the range 3.5 wt. % ⁇ Mn ⁇ 8.5 wt. %.
  • the carbon content of the steel products of the invention is generally rather low.
  • the carbon content is optional in all embodiments. That is, the carbon content is in the range C 1 wt. % in the invention. Embodiments in which the carbon content is in one of the following ranges are particularly preferred
  • the first temperature treatment process is carried out in a continuous strip plant (annealing plant).
  • annealing plant This process is also known as continuous annealing.
  • another possibility is a discontinuous heat treatment (hood-type annealing) of the steel intermediate product.
  • the first temperature treatment of the invention can also be carried out by a special temperature control during hot rolling.
  • a special temperature control care is taken to ensure that the rolling end temperature of the hot strip during hot rolling is in the range above the critical temperature limit T KG .
  • the second temperature treatment process is carried out in a discontinuously operating plant, wherein the steel intermediate product is subjected to the annealing process in this plant in a protective gas atmosphere.
  • This process is preferably carried out in a hood-type annealing plant.
  • the second temperature treatment process can also be carried out in all embodiments in a continuous strip plant (annealing plant) or in a hot-dip galvanizing plant.
  • the steel intermediate product of all embodiments may optionally be subjected to a skin-pass rolling process, which is primarily directed to conditioning the surface of the steel intermediate product.
  • a more intensive skin-pass rolling is not required because the steel intermediate products of the invention have a low Lüders strain.
  • the degree of skin-pass rolling can be reduced or completely avoided.
  • steel intermediate products can be produced which have a tensile strength R m (also called minimum strength) which is greater than 490 MPa.
  • the invention can be used, for example, to provide cold rolled steel products in the form of cold rolled flat products (e.g. coils).
  • the invention can also be used, for example, to produce thin sheets or also wires and wire products.
  • the invention can also be used to provide hot strip steel products.
  • FIG. 1 shows a highly schematic diagram in which the (minimum) total elongation (A 80 ) is plotted in percent versus the tensile strength (R m ) in MPa for various steels for the automotive industry;
  • FIG. 2 shows a schematic stress-strain diagram of a steel product, which has a pronounced yield strength (Lüders strain A L );
  • FIG. 3 shows a schematic diagram showing the two temperature treatment processes
  • FIG. 4 shows in the form of a schematic diagram the critical Temperature T K and the course of the corresponding critical temperature limit T KG ;
  • FIG. 5 shows a schematic diagram, which on the one hand shows the Lüders strain A L in percent and on the other hand the average original austenite grain size (D UAK M ) as a function of the first annealing temperature T 1 , wherein, in this diagram, the corresponding curves of two different samples are shown;
  • FIG. 6 shows a schematic diagram showing the tension ⁇ in MPa as a function of elongation ⁇ in % (analogous to FIG. 2 ), wherein four identical alloys were subjected in this case to four different temperature treatment processes.
  • steel products or steel intermediate products are concerned which are characterized by a special microstructure constellation and properties.
  • intermediate steel products is sometimes used when it is intended to stress that the finished steel product is not concerned but instead a preliminary or intermediate product in a multi-stage production process.
  • the starting point for such manufacturing processes is usually a melt.
  • the alloy composition of the melt is given, since on this side of the manufacturing process, it is possible to influence the alloy composition relatively accurately (for example, by adding components such as alloying elements and optional micro-alloying elements).
  • the alloy composition of the steel intermediate product usually deviates only insignificantly from the alloy composition of the melt.
  • Quantities or content information are given here largely in weight percent (in short wt. %), unless stated otherwise. If information is provided on the composition of the alloy, or the steel product, respectively, then the composition includes, in addition to the explicitly listed materials or substances, iron (Fe) as basic material and so-called unavoidable impurities that always occur in the molten bath and that also show up in the resulting steel intermediate product. All statements in wt. % must always be added to 100 wt. % and all % by volume must always be added to 100% of the total volume.
  • the temperature treatment of the steel intermediate product comprises a first temperature treatment process S. 1 and a subsequent second temperature treatment process S. 2 . These two temperature treatment processes S. 1 and S. 2 are shown in FIG. 3 in two temperature-time diagrams shown next to one another.
  • the first temperature treatment process S. 1 is a high-temperature process in which the steel intermediate product is subjected to a first annealing temperature T 1 during a first holding period ⁇ 1 (this step is also referred to as holding H 1 ).
  • the annealing temperature T 1 lies above a critical temperature limit T KG during the holding H 1 .
  • This critical temperature limit T KG is dependent (inter alia) on the manganese content Mn of the alloy of the manganese steel intermediate product, as determined by numerous examinations.
  • the critical temperature T K represented by the straight line 7
  • the course of the corresponding critical temperature limit T KG represented by the straight line 8
  • FIG. 4 shows by way of example the measurement results of four samples on the basis of small circle symbols. Further details on these four exemplary samples and on further samples of the invention are shown in Tables 1 and 2.
  • Type 1 950 660 522 820 30.7 21.4 0 22 7
  • the alloy composition of the respective type is shown in Table 1, wherein only the essential alloying components are mentioned here. For each type, there are a number of embodiments that have been tested. The corresponding examples are numbered in the left column in Table 2 with the numbers 1 to 26 .
  • Type 4, 18 represents, for example, the alloy composition of Type 4, Example No. 18.
  • T K (866 ⁇ S K *manganese content) (1)
  • the absolute value 866 in degrees Celsius defines the intersection with the vertical axis and the value S K defines the slope. S K is therefore also called the slope value.
  • the slope value S K is preferably 7.83 ⁇ 10% in all embodiments.
  • the critical temperature T K for alloy compositions according to the invention always lies above a lower critical temperature limit T KG .
  • This lower critical temperature limit T KG is shown in FIG. 4 as a straight line 8 .
  • This straight line 8 can be circumscribed by the following equation (2), wherein T KG is given in degrees Celsius:
  • the straight line 8 lies parallel to the straight line 7 .
  • the first annealing temperature T 1 must always be above the lower critical temperature limit T KG to ensure that a manganese steel intermediate product is obtained in which the Lüders strain A L is less than 3%.
  • the second temperature treatment process S. 2 has an influence on the Lüders strain.
  • the second annealing temperature T 2 In order to maintain the grain size of the austenite grains in the structure, the second annealing temperature T 2 must be lower than the first annealing temperature T 1 in any case. Since the first annealing temperature T 1 is always above the lower critical temperature limit T KG , it can be concluded that the second annealing temperature T 2 should preferably be below the lower critical temperature limit T KG .
  • the first annealing temperature T 1 is above the temperature limit T KG and that the second annealing temperature T 2 is in the range between A 1 and A 3 .
  • the second temperature treatment S. 2 is also referred to in this case as intercritical annealing.
  • the first holding period ⁇ 1 is preferably at least 10 seconds in all embodiments, and preferably between 10 seconds and 6000 minutes.
  • the second holding period ⁇ 2 is at least 10 seconds in all embodiments.
  • the two holding periods ⁇ 1 and ⁇ 2 are shown only by way of example.
  • the interval between the first temperature treatment process S. 1 and the second temperature treatment process S. 2 can be selected as needed.
  • the second temperature treatment process S. 2 is performed shortly after the first temperature treatment process S. 1 .
  • Preferred embodiments are those in which the first temperature treatment process S. 1 , including the heating E 1 of the steel intermediate product, the holding H 1 of the first annealing temperature T 1 and the cooling Ab 1 of the steel intermediate product takes less than 7000 minutes.
  • Preferred embodiments are those in which the second temperature treatment process S. 2 , including the heating E 2 of the intermediate steel product, the holding H 2 of the second annealing temperature T 2 and the cooling Ab 2 of the steel intermediate product takes less than 6000 minutes and preferably less than 5000 minutes.
  • Lüders strain A L is independent of whether the first temperature treatment process S. 1 and/or the second temperature treatment process S. 2 is/are carried out in a continuous strip plant (for example in a continuous plant) or in a discontinuous plant (for example in a hood-type annealer).
  • the invention can be applied to both cold strip intermediate products and hot strip intermediate products. In both cases, a significant reduction in Lüders strain A L can be seen.
  • FIG. 5 shows both the reduction of Lüders strain A L in percent and the dependence of the average original austenite grain size (D UAK M ) in ⁇ m with increasing annealing temperature T 1 for two exemplary samples of Type 1 and Type 2 (see also Table 1), as follows.
  • the critical temperature limit T KG is ⁇ 820° C. when it is desired to obtain a Lüders strain for this alloy composition of Type 1 which is smaller than 3%.
  • the curve 10 shows the associated course of the average original austenite grain size D UAK M 1 , as a function of the temperature T 1 .
  • a grain size for this is obtained with >3 ⁇ m.
  • the critical temperature limit T KG2 is ⁇ 970° C. when it is desired to obtain a Lüders strain for this alloy composition of Type 2 which is smaller than 3%.
  • the curve 12 shows the corresponding curve of the average original austenite grain size (D UAK M ) as a function of the temperature T 1 .
  • D UAK M average original austenite grain size
  • a grain size for this results with >8 ⁇ m.
  • the micro-alloying element niobium (Nb) has a recognizable influence, which is expressed as a shift of T KG2 (compared to T KG1 ) to a higher critical temperature for A L ⁇ 3%.
  • the curves 10 and 12 in FIG. 5 show that the original austenite grain size increases with increasing temperature T 1 .
  • the lower temperature limit T KG1 can be determined as follows:
  • the corresponding lower temperature limit T KG1 is shown as a dashed vertical line. It can be seen that the alloy compositions of the Type 1 have an average grain size from an annealing temperature T 1 >T KG1 on which is >3 ⁇ m.
  • the lower temperature limit T KG1 is indicated in FIG. 4 by a small black triangle.
  • the lower critical temperature limit T KG2 can be determined as follows:
  • the micro-alloy leads to an increase in the critical temperature limit T KG .
  • the critical temperature limit T KG2 is approx. 150° C. higher than for the alloy compositions of Type 1.
  • the corresponding effective lower critical temperature limit T* KG2 is shown as a dashed vertical line.
  • the resulting average original austenitic grain size is ⁇ 8 ⁇ m in this case.
  • FIG. 6 shows a schematic diagram indicating the tension ⁇ in MPa as a function of the elongation ⁇ in %.
  • the representation of FIG. 6 is to be compared with the representation of FIG. 2 , wherein FIG. 6 shows only a small section.
  • Type 3 alloys of Table 1 four identical samples (Type 3 alloys of Table 1) were compared here.
  • the Type 3 alloys also meet the requirements of the invention. All four samples were each subjected to a first temperature treatment process S. 1 and a subsequent second temperature treatment process S. 2 . All process parameters were identical, except that in the first temperature treatment process S. 1 , the first annealing temperature T 1 was varied as follows (see column 2 of the following Table 3):
  • the alloys of Type 3 had the following main composition in these experiments:
  • the solid curve 13 . 1 of FIG. 6 (Type 3, 14 of Table 2) shows a clearly visible pronounced yield strength and has a Lüders strain of A L ⁇ 2.6%.
  • the curve 13 . 2 represents another exemplary sample (Type 3, 15 of Table 2) of Type 3, wherein here the yield strength is still slightly pronounced.
  • the curve 13 . 4 represents a further exemplary sample of the Type 3, wherein in this case too no pronounced yield strength is visible any more. This concerns Type 3, 17 of Table 2.
  • the corresponding measured values lie in the range of about 700 to 1000 MPa and with a total elongation A 80 in the range of about 20 to 40%.
US16/085,361 2016-03-23 2017-03-10 Method for temperature-treating a manganese steel intermediate product, and steel intermediate product which has been temperature-treated in a corresponding manner Pending US20190071748A1 (en)

Applications Claiming Priority (3)

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EP16162073.7 2016-03-23
EP16162073.7A EP3222734A1 (de) 2016-03-23 2016-03-23 Verfahren zum temperaturbehandeln eines mangan-stahlzwischenprodukts und stahlzwischenprodukt, das entsprechend temperaturbehandelt wurde
PCT/EP2017/055714 WO2017162450A1 (de) 2016-03-23 2017-03-10 Verfahren zum temperaturbehandeln eines mangan-stahlzwischenprodukts und stahlzwischenprodukt, das entsprechend temperaturbehandelt wurde

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CN108884507A (zh) 2018-11-23
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EP3433386A1 (de) 2019-01-30
ES2816065T3 (es) 2021-03-31
KR20180127435A (ko) 2018-11-28
KR102246704B1 (ko) 2021-04-30
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EP3433386B1 (de) 2020-06-17
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